Comparative Behavior of Viscose-Based Supercapacitor Electrodes Activated by KOH, H2O, and CO2

Activated carbons derived from viscose fibers were prepared using potassium hydroxide, carbon dioxide, or water vapor as activation agents. The produced activated carbon fibers were analyzed via scanning electron microscopy and energy dispersive X-ray spectroscopy, and their porosity (specific surface area, total pore volume, and pore size distribution) was calculated employing physisorption experiments. Activated carbon fibers with a specific surface area of more than 2500 m2 g−1 were obtained by each of the three methods. Afterwards, the suitability of these materials as electrodes for electrochemical double-layer capacitors (supercapacitors) was investigated using cyclic voltammetry, galvanostatic measurements, and electrochemical impedance spectroscopy. By combining CO2 and H2O activation, activated carbon fibers of high purity and excellent electrochemical performance could be obtained. A specific capacitance per electrode of up to 180 F g−1 was found. In addition, an energy density per double-layer capacitor of 42 W h kg−1 was achieved. These results demonstrate the outstanding electrochemical properties of viscose-based activated carbon fibers for use as electrode materials in energy storage devices such as supercapacitors.


Introduction
One of the most pressing global challenges is reducing greenhouse gas emissions and fossil fuel consumption to combat global warming. This problem can be solved by energy production from renewable energy sources. Harvesting a power source as abundant as the sun presents certain advantages and it is exploited in photocatalysis and photovoltaics [1,2]. Many nations and global organizations have proposed plans to address the global warming challenge [3]. The EU, for example, intends to cut greenhouse gas emissions by at least 40% by 2030, while increasing energy from renewable sources to at least 32% [4]. Climate neutrality is to be reached by the year 2050, meaning that either no more greenhouse gases will be emitted, or their emissions will be entirely compensated [4]. The usage of renewable energy sources, on the other hand, creates additional challenges. The amount of energy generated by wind or solar energy, for example, fluctuates dramatically over time, posing significant problems for grid stability and power grid management. Energy storage systems are essential in order to utilize renewable energies reliably, sustainably, and consistently.
Supercapacitors are energy storage devices gaining popularity due to their ability to be charged and discharged very rapidly, needing little maintenance, and having a very high power density and a long life of over 1 million charge and discharge cycles [5][6][7][8]. Carbon materials are commonly used to fabricate electrodes for such supercapacitors because they Nanomaterials 2022, 12, 677 2 of 11 are easy to process and are chemically and thermally stable. Moreover, their structural properties can be easily modified and optimized. Activated carbons are widely used electrode materials because they have a large specific surface area (1000-3000 m 2 g −1 ) and a high total pore volume (0.5-2 cm 3 g −1 ) at a reasonable cost (3.65 € kg −1 ) [9][10][11]. In the last two decades, the interest in sustainable carbon precursors increased drastically, and all sorts of biomass have been tested as precursors for activated carbon [12][13][14]. However, the availability and consistency of the material quality is always an issue that has to be considered when using natural materials [15]. Fibrous precursors are of special interest, as activated carbon fibers (ACFs) are a thrilling alternative to traditional granular and powdered activated carbons (ACs). The great advantage of ACFs is their low electrical resistance along the fiber axis and the excellent contact with the current collector [16,17]. For achieving the required carbon properties, a number of chemical and physical activation routes have been developed for increasing carbon surface areas and developing the pore network in carbon materials [18][19][20]. Despite this, fibrous activated carbon materials made from bio-based precursors have been poorly studied. This is partly due to the fact that only high-purity materials such as viscose or lignin fibers can be used due to the consistency of the material quality. Another reason for the lack of publications is the carbonization and activation process, which must be selected in such a way that the fiber structure is at least partially retained, even in the electrode. Based on these findings, in the current work, viscose fibers were chosen as precursor material. These are artificially-made fibers from bio-based resources, thus combining sustainability and availability in good and constant quality, while also offering the full advantage of fibrous materials. Three different activation methods are applied, and their effects on the porosity of the ACFs and their properties on the electrochemical performance of the supercapacitor are investigated. The physical activation after carbonization by means of carbon dioxide and water vapor is considered. In addition, the chemical activation by means of potassium hydroxide, which takes place during the carbonization step, is examined.

Preparation of the Activated Carbon Fibers
After drying for 12 h at 90 • C, viscose fibers (1.7 dtex, 38 mm) were treated with a 37.9 mmol L -1 DAHP solution for 15 min. The fibers were dried again (12 h at 90 • C) before being carbonized in nitrogen atmosphere in a chamber furnace (HTK8, Carbolite Gero GmbH, Neuhausen, Germany). The temperature program consisted of a heating ramp of 10 • C min −1 up to 850 • C and an isothermal step at this temperature for 30 min.
The activation with H 2 O and/or CO 2 was done after carbonization in a rotary kiln (RSR-B 120/500/11, Nabertherm GmbH, Lilienthal, Germany). The furnace was heated to 870 • C under nitrogen and kept isothermal for 30 min prior to the actual activation. A gas flow of 80 L h −1 for 180 min was used for the CO 2 activation. For the activation with H 2 O, 1.0 mL min −1 of water was injected with a peristaltic pump for 180 min.
Activation using KOH took place during the carbonization step. The literaturerecommended approach of mixing the precursor with four times the amount of KOH and subsequent carbonization did not work, as the fiber structure should not be compromised due to grinding with KOH. [21]. Instead, the DAHP-impregnated and dried viscose fiber was impregnated again with a 50 wt.% KOH solution. The ACF made like this was washed several times with a 10% HCl solution and with distilled H 2 O until a neutral pH was achieved.

Electrode Fabrication and Electrochemical Characterization
The ACFs were ground in a mortar mill (RM 200, Retsch GmbH, Haan, Germany). After adding 10 wt.% graphite (C-nergy KS-L, Imerys, Paris, France) and 10 wt.% polytetrafluoroethylene (PTFE; Sigma Aldrich, St. Louis, MO, USA), the ACFs were ground again until a kneadable dough was obtained. This dough was rolled out to a thickness of Nanomaterials 2022, 12, 677 3 of 11 90-100 µm using a sheet metal roller, and electrodes were punched out. The electrodes were dried in vacuo overnight at 110 • C.
Two symmetrical electrodes soaked with a 1 M triethylmethylammonium tetrafluoroborate (TEMA BF 4 , TCI Deutschland GmbH, Eschborn, Germany) solution in propylene carbonate (PC, Acros Organics N.V., Geel, Belgium) were used in a Swagelok ® -type 2electrode test cell. To prevent a short circuit, a separator (Celgard ® 3401, Celgard LLC, Charlotte, NC, USA) was used between the electrodes. C-coated aluminum foil was employed as current collector (z-flo 2651, Coveris Management GmbH, Vienna, Austria). All cells were built under an argon atmosphere.
A potentiostat (Vertex.One, IviumTechnologies BV, Eindhoven, The Netherlands) was used for electrochemical impedance spectroscopy (EIS) measurements, cyclic voltammetry (CV), and galvanostatic discharge curves (GDC). EIS measurements were conducted with 10 mV of AC voltage amplitude in the frequency range of 1 MHz-0.01 Hz. The gravimetric capacitance C S was calculated from CV and GDC data using Equations (1) and (2): The specific capacitance C S,CV of one electrode was determined by the integral i · dV of the positive part of the 5th CV curve, limited by V f and V i of the cell voltage ∆V, scan rate v, and the mass of the active material m E of one electrode. For the GDC measurements, C S,GDC was calculated using the current i, the discharge time t, m E and ∆V. The energy density E S and power density P S for a device were calculated using Equations (3) and (4):

Structural Characterization
A volumetric sorption analyzer (Autosorb-iQ, Anton Paar QuantaTec Inc, Boynton Beach, FL, USA) was used to determine the specific surface area, pore size distribution, and total pore volume of the ACFs by N 2 isothermal adsorption (77 K). The samples were degassed for 2 h at 350 • C. The non-local density functional theory (NLDFT) and the Brunauer-Emmett-Teller (BET) method were used to compute the pore size distribution (PSD) and the specific surface area S BET [22,23]. At a relative pressure of 0.99, the total pore volume V tot was estimated to be equal to the liquid volume of the adsorbate (N 2 ).
An Ultim Max 100 EDX detector (Oxford Instruments, Abington, United Kingdom) coupled to a scanning Auger electron spectroscopy microscope (JAMP-9500F, JEOL Ltd., Akishima, Japan) was used to characterize structural and elemental properties of the samples. Energy-dispersive X-ray spectroscopy (EDX) measurements were performed at an acceleration voltage of 5 kV. The system was also used to take scanning electron microscopy (SEM) images.

Results and Discussion
To achieve qualitative comparability, the activation conditions were chosen so that ACFs with S BET of around 2500 m 2 g −1 were produced. CO 2 has been previously studied, and the prepared AFC yielded very good results in supercapacitor electrodes [24]. In the current study, activation by H 2 O using identical activation temperature and time yielded comparable ACFs. For KOH activation, a completely different approach had to be used. Here, the DAHP-impregnated and dried fiber was treated again with a 50 wt.% KOH solution. After drying, chemical activation took place simultaneously with the carbonization step. In physical activation with CO 2 or H 2 O, carbon is partially gasified by the oxidant. The gasification of carbon by CO 2 is dependent on the Boudouard reaction [25]. This reaction describes the equilibrium between CO 2 and CO that is established during the reaction with carbon Equation (5). High temperatures shift the equilibrium to the product side (CO) due to the endothermic reaction. In this way, carbon in the sample was partially gasified.
C + CO 2 2 CO Activation with H 2 O as the activating gas works according to the water gas equilibrium equation (Equation (5)), in which carbon and steam are in equilibrium with CO and hydrogen gas. A detailed description of this reaction, which can be very complex, can be found in the corresponding literature [25,26].
With the use of KOH, the carbon skeleton was additionally intercalated and expanded by potassium [18]. All three tested activation techniques led to ACFs reaching the desired range of S BET = 2500 m 2 g −1 ( Table 1). The ACF activated with CO 2 had the highest S BET of 2737 m 2 g −1 . The high S BET attained here is not surprising, given that activation by CO 2 has been extensively investigated, and the effects of DAHP as an impregnating agent have also been described previously [24,27]. H 2 O-and KOH-activated fibers showed a marginally lower S BET of 2553 m 2 g −1 and 2516 m 2 g −1 , respectively. With 1.35 cm 3 g −1 , the CO 2 -activated sample showed the highest V tot . The H 2 O-activated ACF had with 1.27 cm 3 g −1 a higher V tot than the KOH-activated sample (1.10 cm 3 g −1 ). Table 1. Data on the porosity (specific surface area S BET and total pore volume V tot ) and the total yield of the ACFs.

Activation Agent
S BET /m 2 g −1 V tot /cm 3  The total yield calculated from the difference of the mass of dried viscose fiber and ACF divided by the mass of dried fiber is also shown in Table 1. The total yield of the KOH activation was the lowest at 2.1%. In addition to the formation of pores, this was due to the fact that a very fine powder was produced, which had to be washed several times. The yield of activation using CO 2 was much higher at 9.2%. The highest total yield of 23.9% was achieved with activation using H 2 O. The total yield of ACFs activated with CO 2 or H 2 O was composed of the partial yields of the carbonization step and the activation step [24]. The carbonization yield in both cases was 31%.
The PSD (Figure 1b) calculated from the adsorption isotherms ( Figure 1a) using nitrogen at 77 K explains why the H 2 O-activated ACF had a higher V tot at lower S BET than the KOH-activated ACF. The AC produced by KOH activation had pores with a diameter d P < 0.7 nm and in the range of d P = 1.0-2.5 nm. On the other hand, activation with CO 2 or H 2 O hardly led to pores smaller than 0.9 nm. The majority of the pores had a diameter of d P = 0.9-3.5 nm. The CO 2 -activated sample had a larger pore volume (around 2.5 nm) than the water-activated ACF. The H 2 O-activated fiber was the only sample to show pores with a diameter around 3.7 nm. the water-activated ACF. The H2O-activated fiber was the only sample to show pores with a diameter around 3.7 nm. The CVs of the EDLCs were recorded at a scan rate of 10 mV s −1 with a potential window of −2.7-2.7 V (Figure 2a). Decomposition of the electrolyte did not occur at a potential window of ±2.7 V, as was already demonstrated [28][29][30]. The test cell prepared from the CO2and the H2O-activated fibers had a quasi-rectangular shape, which is typical for EDLCs. The KOH-activated sample showed a parallelogram, indicating a higher internal resistance [31]. A similar trend could be seen in the GDCs measured at 1.0 A g −1 (Figure 2b). While the EDLC made from CO2-activated ACFs showed a relatively small internal resistance (IR) drop, the other two samples had a much stronger decline. The calculated equivalent series resistance (ESR) was 584 Ω for the KOH-activated sample, 430 Ω for the H2O-activated sample, and only 254 Ω for the CO2-activated EDLC. The specific capacitance CS,CV, derived from the CVs at various scan rates v, is shown in Figure 2c. At the smallest scan rate studied (1 mV s -1 ), the highest specific capacitance was achieved. The H2O-activated sample showed the largest specific capacitance at 180 F g −1 , the electrode made of CO2-activated fibers 171 F g −1 , and the KOH-activated sample 166 F g −1 . This trend persisted at more rapid scan rates. Even at very fast scan rates of 300 mV s −1 , the investigated EDLCs still reached values of 45 F g −1 (H2O), 34 F g −1 (CO2), and 24 F g −1 (KOH). Evaluation of specific capacitance by GDC is recommended over that by CV because side reactions can occur, especially at the edges of the potential window, which can enlarge the specific capacitance calculated by CV [32]. The calculated specific capacitance CS,GDC of the samples (Figure 2d) behaved slightly differently than that of CS,CV. Here, the KOH-activated sample showed the maximum specific capacitance of 140 F g −1 at the lowest specific current IS of 0.1 A g −1 . For the electrodes produced from CO2-activated ACFs, CS,GDC was 121 F g −1 , and for the H2O-activated fibers, 112 F g −1 . With the increase of IS, a larger voltage drop occurred, probably caused by the high internal resistance of the KOH sample, causing CS,GDC to drop sharply. At currents of 2.0 A g −1 and higher, the IR drop was so large that no specific capacitance could be determined. The best performance at discharge currents above 0.6 A g -1 was shown by the CO2-activated sample. From the GDCs, the specific energy ES and the specific power PS of the complete EDLC (not per electrode) were calculated and are shown in a Ragone plot (Figure 2e). The highest power of 1360 W kg −1 was obtained with the CO2-activated electrodes, followed by the H2O-activated (626 W kg −1 ) and the KOH-activated electrodes (410 W kg −1 ). Additionally, the highest specific energy of 25.9 W h kg −1 was achieved by the CO2-activated fibers. The other two samples reached specific energies of 20.8 W h kg −1 (H2O) and 18.9 W h kg −1 (KOH) per device, respectively. The CVs of the EDLCs were recorded at a scan rate of 10 mV s −1 with a potential window of −2.7-2.7 V (Figure 2a). Decomposition of the electrolyte did not occur at a potential window of ±2.7 V, as was already demonstrated [28][29][30]. The test cell prepared from the CO 2 -and the H 2 O-activated fibers had a quasi-rectangular shape, which is typical for EDLCs. The KOH-activated sample showed a parallelogram, indicating a higher internal resistance [31]. A similar trend could be seen in the GDCs measured at 1.0 A g −1 (Figure 2b). While the EDLC made from CO 2 -activated ACFs showed a relatively small internal resistance (IR) drop, the other two samples had a much stronger decline. The calculated equivalent series resistance (ESR) was 584 Ω for the KOH-activated sample, 430 Ω for the H 2 O-activated sample, and only 254 Ω for the CO 2 -activated EDLC. The specific capacitance C S,CV , derived from the CVs at various scan rates v, is shown in Figure 2c. At the smallest scan rate studied (1 mV s -1 ), the highest specific capacitance was achieved. The H 2 O-activated sample showed the largest specific capacitance at 180 F g −1 , the electrode made of CO 2 -activated fibers 171 F g −1 , and the KOH-activated sample 166 F g −1 . This trend persisted at more rapid scan rates. Even at very fast scan rates of 300 mV s −1 , the investigated EDLCs still reached values of 45 F g −1 (H 2 O), 34 F g −1 (CO 2 ), and 24 F g −1 (KOH). Evaluation of specific capacitance by GDC is recommended over that by CV because side reactions can occur, especially at the edges of the potential window, which can enlarge the specific capacitance calculated by CV [32]. The calculated specific capacitance C S,GDC of the samples (Figure 2d) behaved slightly differently than that of C S,CV . Here, the KOH-activated sample showed the maximum specific capacitance of 140 F g −1 at the lowest specific current I S of 0.1 A g −1 . For the electrodes produced from CO 2 -activated ACFs, C S,GDC was 121 F g −1 , and for the H 2 O-activated fibers, 112 F g −1 .
With the increase of I S , a larger voltage drop occurred, probably caused by the high internal resistance of the KOH sample, causing C S,GDC to drop sharply. At currents of 2.0 A g −1 and higher, the IR drop was so large that no specific capacitance could be determined. The best performance at discharge currents above 0.6 A g -1 was shown by the CO 2 -activated sample. From the GDCs, the specific energy E S and the specific power P S of the complete EDLC (not per electrode) were calculated and are shown in a Ragone plot (Figure 2e). The highest power of 1360 W kg −1 was obtained with the CO 2 -activated electrodes, followed by the H 2 O-activated (626 W kg −1 ) and the KOH-activated electrodes (410 W kg −1 ). Additionally, the highest specific energy of 25.9 W h kg −1 was achieved by the CO 2 -activated fibers. The other two samples reached specific energies of 20.8 W h kg −1 (H 2 O) and 18.9 W h kg −1 (KOH) per device, respectively. The morphology of the electrodes was examined by SEM ( Figure 3). The electrodes from the CO2-and H2O-activated ACFs displayed a very similar morphology, including fibrous parts. The electrode made from the KOH-activated sample showed hardly any clear fibrous features. Only granular pieces and fibrous fragments could be found. This was already evident after activation. While the fiber structure was completely preserved during activation with CO2 or H2O, KOH activation resulted in a powder. During activation with KOH, metallic potassium intercalated into the carbon lattice and expanded it [18,33]. This expansion seemed to destroy the fibrous structure of the sample.  The morphology of the electrodes was examined by SEM ( Figure 3). The electrodes from the CO 2 -and H 2 O-activated ACFs displayed a very similar morphology, including fibrous parts. The electrode made from the KOH-activated sample showed hardly any clear fibrous features. Only granular pieces and fibrous fragments could be found. This was already evident after activation. While the fiber structure was completely preserved during activation with CO 2 or H 2 O, KOH activation resulted in a powder. During activation with KOH, metallic potassium intercalated into the carbon lattice and expanded it [18,33]. This expansion seemed to destroy the fibrous structure of the sample. The morphology of the electrodes was examined by SEM ( Figure 3). The electrodes from the CO2-and H2O-activated ACFs displayed a very similar morphology, including fibrous parts. The electrode made from the KOH-activated sample showed hardly any clear fibrous features. Only granular pieces and fibrous fragments could be found. This was already evident after activation. While the fiber structure was completely preserved during activation with CO2 or H2O, KOH activation resulted in a powder. During activation with KOH, metallic potassium intercalated into the carbon lattice and expanded it [18,33]. This expansion seemed to destroy the fibrous structure of the sample.    (Table 2) were used to examine the effect of the activation method on the chemical composition. The electrode activated by KOH had only oxygen as a heteroatom with a content of 2.6 at.% and therefore a high carbon content of 97.4 at.%. The multiple washing steps of the AC with HCl and H 2 O probably resulted in this low amount of heteroatoms despite impregnation. It must be noted here that neither the CO 2 -activated nor the H 2 O-activated fibers were washed after activation. The influence of the impregnation using DAHP was clearly detectable on the electrode made from CO 2 -activated fibers. The carbon content was the lowest at 88.3 at.%, and in addition, oxygen (8.0 at.%), phosphorus (2.9 at.%), and nitrogen (0.9 at.%) could be found. In contrast, the electrode from the H 2 O-activated fibers was very pure. The carbon content was very high at 98.6 at.%, with only 1.4 at.% oxygen. Due to otherwise identical conditions, it can be concluded that the heteroatoms were washed out during H 2 O activation. In addition to the previous electrochemical measurements, the EDLCs were characterized using EIS, and the data were fitted to an equivalent circuit (Figure 4). The resistances R1 and R2 of the test cells calculated by fitting are shown in Figure 4c. The KOH-activated sample had the highest serial resistance R1 of 265 mΩ. The reason for this may be linked to the morphology of the electrode showing an increased grain boundary area/volume (see Figure 3c). While the other two electrodes consisted at least partly of fibers, along whose axis the electrical resistivity was low, the KOH electrode consisted of almost granular particles with many interfaces, whereby the resistance was higher. For the charge-transfer resistance R2, the picture was different. In contrast to the H 2 O-activated sample (R2 = 39 mΩ), the CO 2 -activated sample showed a relatively high charge-transfer resistance R2 of 370 mΩ. These findings contradict Ma et al., who found that P-doping decreases the charge-transfer resistance via improving the electrode's wettability [34]. The charge-transfer resistance strongly depends on the accessibility of the pores by the electrolyte [16]. The pores in the H 2 O-activated sample with a diameter around 3.7 nm (see Figure 1b) could lead to better accessibility, which could outweigh the effect of P-doping. Nanomaterials 2022, 12, x FOR PEER REVIEW 7 of 11 EDX spectra (Table 2) were used to examine the effect of the activation method on the chemical composition. The electrode activated by KOH had only oxygen as a heteroatom with a content of 2.6 at.% and therefore a high carbon content of 97.4 at.%. The multiple washing steps of the AC with HCl and H2O probably resulted in this low amount of heteroatoms despite impregnation. It must be noted here that neither the CO2-activated nor the H2O-activated fibers were washed after activation. The influence of the impregnation using DAHP was clearly detectable on the electrode made from CO2-activated fibers. The carbon content was the lowest at 88.3 at.%, and in addition, oxygen (8.0 at.%), phosphorus (2.9 at.%), and nitrogen (0.9 at.%) could be found. In contrast, the electrode from the H2O-activated fibers was very pure. The carbon content was very high at 98.6 at.%, with only 1.4 at.% oxygen. Due to otherwise identical conditions, it can be concluded that the heteroatoms were washed out during H2O activation. In addition to the previous electrochemical measurements, the EDLCs were characterized using EIS, and the data were fitted to an equivalent circuit (Figure 4). The resistances R1 and R2 of the test cells calculated by fitting are shown in Figure 4c. The KOHactivated sample had the highest serial resistance R1 of 265 mΩ. The reason for this may be linked to the morphology of the electrode showing an increased grain boundary area/volume (see Figure 3c). While the other two electrodes consisted at least partly of fibers, along whose axis the electrical resistivity was low, the KOH electrode consisted of almost granular particles with many interfaces, whereby the resistance was higher. For the charge-transfer resistance R2, the picture was different. In contrast to the H2O-activated sample (R2 = 39 mΩ), the CO2-activated sample showed a relatively high chargetransfer resistance R2 of 370 mΩ. These findings contradict Ma et al., who found that Pdoping decreases the charge-transfer resistance via improving the electrode's wettability [34]. The charge-transfer resistance strongly depends on the accessibility of the pores by the electrolyte [16]. The pores in the H2O-activated sample with a diameter around 3.7 nm (see Figure 1b) could lead to better accessibility, which could outweigh the effect of Pdoping. Since a longer activation time with CO 2 resulted in very poor yield, the specific surface area of the ACFs could not be further increased using CO 2 . Following the finding that H 2 O activation also achieved very good results, an attempt was made to first activate the carbonized fiber impregnated with DAHP using CO 2 and then to further increase the surface area using H 2 O. The parameters for the CO 2 activation were set to be identical to those of the previous CO 2 activation, followed by 1 h of H 2 O activation with 1 mL min −1 at 870 • C.
The N 2 isotherms and the PSDs derived are displayed in Figure 5. By H 2 O activation following the CO 2 activation, the specific surface area S BET could be increased from 2737 m 2 g −1 to 2850 m 2 g −1 , while V tot increased from 1.352 cm 3 g −1 to 1.577 cm 3 g −1 . Up to a pore diameter d P of 1.7 nm, the PSD behaved almost identically. Thus, it seems that the H 2 O activation had no effect on pores in this region. Pores having a larger diameter were widened by the second activation, increasing the pore diameter. The yield decreased from 9.2% to 6.4% due to the additional H 2 O activation, which was still a significantly higher total yield than could be achieved using KOH activation.   Since a longer activation time with CO2 resulted in very poor yield, the specific surface area of the ACFs could not be further increased using CO2. Following the finding that H2O activation also achieved very good results, an attempt was made to first activate the carbonized fiber impregnated with DAHP using CO2 and then to further increase the surface area using H2O. The parameters for the CO2 activation were set to be identical to those of the previous CO2 activation, followed by 1 h of H2O activation with 1 mL min −1 at 870 °C.
The N2 isotherms and the PSDs derived are displayed in Figure 5. By H2O activation following the CO2 activation, the specific surface area SBET could be increased from 2737 m 2 g −1 to 2850 m 2 g −1 , while Vtot increased from 1.352 cm 3 g −1 to 1.577 cm 3 g −1 . Up to a pore diameter dP of 1.7 nm, the PSD behaved almost identically. Thus, it seems that the H2O activation had no effect on pores in this region. Pores having a larger diameter were widened by the second activation, increasing the pore diameter. The yield decreased from 9.2% to 6.4% due to the additional H2O activation, which was still a significantly higher total yield than could be achieved using KOH activation. The double activated fiber was further characterized by CV and GDC. Potential windows of ±2.0 V and ±2.7 V were examined. Specific capacitances of up to 118.4 F g −1 derived by CV were achieved for the voltage window of ±2.0 V (Figure 6a). With increases of the voltage window, CS,CV also increased at all scan rates. A very high value of CS,CV = 240 F g −1 could be achieved at the slowest scan rate (1.0 mV s −1 ). In the GDC measurements ( Figure  6b), specific capacitances of 122 F g −1 were obtained for discharging from 2.0 V, and 178 F g −1 for discharging from 2.7 V (at very low specific current of 0.025 A g −1 ). At higher currents, the sample with the higher initial voltage showed the lower specific capacitance. For the supercapacitor charged to 2.0 V, the specific power PS calculated from the GDCs reached 4823 W kg −1 (Figure 6c). The maximum energy density ES achieved was 16.5 W h kg −1 . When charging to 2.7 V, a specific power PS of 3640 W kg −1 was accomplished. The maximum specific energy ES was 42.4 W h kg −1 , which is extremely high compared to previously-reported energy densities [10,35,36]. The double activated fiber was further characterized by CV and GDC. Potential windows of ±2.0 V and ±2.7 V were examined. Specific capacitances of up to 118.4 F g −1 derived by CV were achieved for the voltage window of ±2.0 V (Figure 6a). With increases of the voltage window, C S,CV also increased at all scan rates. A very high value of C S,CV = 240 F g −1 could be achieved at the slowest scan rate (1.0 mV s −1 ). In the GDC measurements (Figure 6b), specific capacitances of 122 F g −1 were obtained for discharging from 2.0 V, and 178 F g −1 for discharging from 2.7 V (at very low specific current of 0.025 A g −1 ). At higher currents, the sample with the higher initial voltage showed the lower specific capacitance. For the supercapacitor charged to 2.0 V, the specific power P S calculated from the GDCs reached 4823 W kg −1 (Figure 6c). The maximum energy density E S achieved was 16.5 W h kg −1 . When charging to 2.7 V, a specific power P S of 3640 W kg −1 was accomplished. The maximum specific energy E S was 42.4 W h kg −1 , which is extremely high compared to previously-reported energy densities [10,35,36].

Conclusions
Three different ways of obtaining activated carbon from DAHP-impregnated viscose fiber and using it as electrode material for supercapacitors were investigated. It was shown that activation by CO 2 or H 2 O yields ACFs with a high specific surface area and a PSD that is very suitable for use as an electrode material for supercapacitors. Unlike activation with KOH, which requires immense amounts of chemicals and additional washing steps, here the fiber structure was preserved, resulting in cells with remarkably low internal resistance. The H 2 O activation also allowed the removal of the majority of heteroatoms without the need for a subsequent washing step, as shown by EDX analysis. By combining the two activation methods involving CO 2 and H 2 O, ACFs could finally be produced. Due to their porosity with pores between 0.5 and 5.5 nm and a specific surface area of 2850 m 2 g −1 , morphology and purity were ideally suited for use in EDLCs. Thus, supercapacitors could be produced that exceeded a specific capacitance of 178 F g −1 per electrode (calculated from GDC) and an energy density of 42 W h kg −1 for the device. Funding: The authors wish to thank the European Regional Development Fund (EFRE) and the province of Upper Austria for financial support of this study through the program IWB 2014-2020 (project BioCarb-K).